TW201139699A - Non-oriented magnetic steel sheet - Google Patents

Abstract

Disclosed is a non-oriented magnetic steel sheet which contains 0.3-5.3% by mass of Cr, 1.5-4% by mass of Si, 0.4-3% by mass of Al and 0.0003-0.01% by mass of W. The non-oriented magnetic steel sheet has a C content of 0.006% by mass or less, an Mn content of 1.5% by mass or less, an S content of 0.003% by mass or less and an N content of 0.003% by mass or less, and the balance is made up of Fe and unavoidable impurities.

Description

201139699 VI. Description of the invention: Technical field of the invention of the invention 3. Field of the Invention The present invention relates to a non-oriented electrical steel sheet suitable for a core material of a motor. C. Prior Art 3 In recent years, in the field of electric equipment using non-directional electromagnetic steel sheets, there has been a demand for energy saving, and motors for cooling and heating machines, driving motors for electric vehicles, and the like are being further reduced in power consumption. Further, the control of the drive motor replaces the ON-OFF control of the current, and the PWM (pulse width modulation) waveform control in which the inverter is harmonically overlapped is now mainstream. Therefore, excellent non-directional electromagnetic steel sheets are being pursued for superior high frequency characteristics. In the past, in order to improve the high-frequency iron loss of the non-oriented electrical steel sheet, a method of increasing the contents of Si, A1, and Cr to increase the specific resistance and to reduce the thickness of the non-oriented electrical steel sheet as much as possible has been carried out. According to these methods, the eddy current loss can be reduced. However, in the non-oriented electrical steel sheet containing Cr, Cr-based carbides are precipitated during the manufacturing process and after the manufacturing process, and the iron loss is increased and deteriorated. In the annealing of the manufacturing process, there is a case where Cr-based carbides are precipitated. Further, among the customers who use the non-oriented electrical steel sheet, there are cases where the combustion of the stamping oil disappears, the shrinkage of the separated iron core is produced, and the stress relief annealing is performed. These processes are performed at a temperature lower than about 200 ° C to 750 ° C, 201139699, and at this time, lanthanide carbides are precipitated at grain boundaries. . Here, it has been proposed to contain M in order to suppress precipitation of g-based carbides in a non-oriented electrical steel sheet containing Cr. However, in the technique, the high-priced M〇 content is 0.05 mass% or more, and the material cost is remarkably increased. PRIOR ART DOCUMENT PATENT DOCUMENT Patent Document 1: Japanese Patent Laid-Open Publication No. 2002-294417 (2) Patent Document 3: Japanese Patent Laid-Open Publication No. Hei 2 No. Hei 2 No. Hei. OBJECTS OF THE INVENTION PROBLEMS TO BE SOLVED BY THE INVENTION The present invention has an object of providing a non-oriented electrical steel sheet which can suppress an increase in cost and has higher frequency characteristics. Means for Solving the Problems The present invention is as follows. (1) A non-oriented electrical steel sheet comprising Cr: 0.3 mass% / 5. 5.3 mass%, Si: 1.5 mass% - 4 mass %, A1: 0.4% by mass to 3% by mass, and W: 0.0003% by mass to 0.01% by mass, C content is 0.006% by mass or less, Μη content is 1.5% by mass or less, and S content is 〇.〇〇3% by mass. The content of niobium is 〇.〇〇3 mass% or less' and the remainder is composed of impurities that can be avoided by ?6 and not 201139699. (2) Non-directional electrical steel sheets of (1) with mass%, Ti: 3 It is at least one selected from the group consisting of M〇: 3 薏0/〇~0.007 mass 〇/〇, and Nb: 0.2% by mass to 0.004% by mass. (7) Non-directional electromagnetic as in (1) postal) The steel sheet, which is further contained, is selected from the group consisting of V: 〇.〇〇〇5f S〇^〇.〇〇5 ft〇/〇. 2r : 〇.〇〇〇3f t〇/〇^〇〇〇3f%, Cu : 0.0〇1% by mass to 〇2 by mass, : 0.001% by mass of 〇·2% by mass, Ni: 0. 〇〇1% by mass of 〇2 贝Berry/〇, Sb. 〇·001% by mass 〇 2% by mass, rare earth, ο. _2 mass% of the side amount, and Ca: 〇 _ mass% to 0.006 mass% of at least one of the groups. EFFECTS OF THE INVENTION According to the present invention, even if Cr is contained, since an appropriate amount is contained, embrittlement can be avoided and the specific resistance can be increased, and precipitation of the ship-based carbide and magnetic attenuation can be reduced, and high-frequency characteristics can be improved. C embodiment; 3 for implementing the invention

Similarly to Si and A1, Cr can increase the specific resistance of the non-oriented electrical steel sheet. Further, unlike Cr and Si, Cr is less likely to embrittle the non-oriented electrical steel sheet. On the other hand, there is a non-oriented electrical steel sheet of Cr, particularly in a non-oriented electrical steel sheet having a Cr content of 3% by mass or more, at 200. (: Cr-based carbides are easily precipitated at temperatures of about ~700 °C. Cr-based carbides are deposited in the form of flakes at the grain boundaries, which is a hindrance to the movement of the magnetic walls. Therefore, high-frequency irons of 4 Hz or higher are particularly required. The damage is remarkably deteriorated. The Cr-based carbide is precipitated at 750. (The temperature is not precipitated at the above high temperature, but is precipitated at a temperature of about 2 〇〇 to about 700 ° C. 201139699 Here, the inventors of the present invention are directed to suppression (Cr) , Fe) 7C3 and other methods for the precipitation of Cr-based carbides. The results show that Cr-based carbides are found in the non-oriented electrical steel sheets containing W in addition to Cr, by the interaction of w and Cr. The precipitation is suppressed, and the deterioration of the iron loss is also suppressed. This reason is not clear yet, but it is considered to be effective as a carbide forming element in the precipitation behavior of the carbide. It has also been found that when Mo, Ti, and/or Nb are contained in addition to Cr and W, the precipitation of Cr-based carbides is further suppressed by the interaction of these elements with Cr. The reason is not yet clear. But think it is & carbonization In the precipitation behavior of the material, it is effective as a carbide-forming element, butadiene' and/or Nb. The details are as follows, when w is contained in a non-oriented electrical steel sheet having a low Cr content, w-carbonization The material will be precipitated, and even if recrystallization annealing is performed at a temperature of about 800 to 1100 C, the growth of the crystal will be hindered, and the crystal grains of the desired size cannot be obtained. Mo, Ti' and Nb are also the same. Therefore, the Cr content is In addition, as described above, since the temperature at which the reaction product is precipitated is low, it is at 8 〇〇 ° C to 1100. (In the recrystallization annealing at a temperature of about 3,000 Å, the carbide does not precipitate. Therefore, the growth of the crystal grains is less likely to be hindered by the Cr-based carbide. The present inventors have found that, in the case of containing an appropriate amount of the non-oriented electrical steel sheet, for example, the so-called magnetic attenuation below, that is, Fe3C ((tetra) carbon iron) The precipitation is also subject to the _ system. The hair date and the like are also found in the case of more, Ti, and / or can, it will further inhibit the precipitation of ¥. "彳L as the temperature of the motor spins rise, the subway damage gradually deteriorates. 6 201139699 phenomenon, It is preferable that the magnetic attenuation is not easily generated in advance. Hereinafter, the embodiment of the present invention will be described in more detail. The non-oriented electrical steel sheet of the present embodiment contains Cr: 〇3 mass/〇5_3 Berry/〇, S1· · J 5 mass% to 4 mass%, u mass mass %, and W: 0.0003 mass% to 〇〇1 mass%. Further, the c content is 〇 _ _ _ 5% or less, and the Mn content is h 5% by mass or less, S The content is 0.003 mass% or less, and the N content is 〇.〇〇3 mass% or less. Further, the remaining portion is composed of unavoidable impurities. When the cerium contains more than 〇.〇〇6 mass%, even if it contains an appropriate amount Buying, etc., sufficiently suppresses the precipitation of lanthanide carbides as _. Further, it is affected by the influence of the anti-sludge, and the south frequency characteristic, especially the high-frequency characteristic at low temperature, is also the cause of magnetic attenuation. Therefore, the c content is set to 〇._, and the other aspect 'industrially lowering the C content to less than (10) (four) mass%' requires a large amount of cost. Therefore, the C content is preferably 0-5 mass% or more. It can avoid embrittlement and increase the specific resistance of non-directional electromagnetic steel sheets. When he is _3, it is not easy to transfer the wire. Further, when the mass is 0.3 mass, the carbide such as w is likely to be precipitated, and it is easy to hinder the growth of the crystal grains which are annealed again. — 5.3 Quality Section, even if it contains an appropriate amount: the surface of the powder is greater than the precipitation of the substance is difficult. In addition, it is "inhibited by the ground". It is (4) 2::: $ is set to 0.3% by mass to 5.3% by mass. Further, C 3 is used, and the α content is preferably 5% by mass or more. In order to reduce the precipitation of Cr-based carbides, the Cr content is preferably 5.0% by mass or less, more preferably 2.5% by mass or less, and the mass is 2.1, and the mass is preferably 1.6% by mass or more. % is better.

The Si system increases the specific resistance to improve the high frequency iron loss. When the Si content is less than 1.5% by mass, it is difficult to sufficiently obtain this effect. On the other hand, when the Si content is more than 4% by mass, cold working becomes difficult due to embrittlement. Therefore, the Si content is set to 1.5% by mass to 4% by mass. Further, in order to further lower the high-frequency iron loss, the Si content is preferably more than 2% by mass. A1 increases the specific resistance and improves the high-frequency iron loss. When the A1 content is less than 0.4% by mass, it is difficult to sufficiently obtain the effect. On the other hand, when the A1 content is more than 3% by mass, cold working is difficult due to embrittlement. Further, the higher the A1 content, the lower the magnetic flux density and the tendency to deteriorate. Therefore, the A1 content is set to 0.4% by mass to 3% by mass. When the content of Μη is more than 1.5% by mass, the brittleness becomes remarkable. Therefore, the Μη content is set to 1.5 mass or less. On the other hand, when the content of Μη is 0.05% by mass or more, the specific resistance is effectively increased to reduce the iron loss. Therefore, the Μη content is preferably 0.05% by mass or more. When the S content is more than 0.003 mass%, the formation of a sulfide such as Μ n S becomes remarkable, and accordingly, the movement of the magnetic wall is hindered and the magnetic properties are deteriorated. Therefore, the S content is made 0.003 mass% or less. On the other hand, industrially, in order to reduce the S content to less than 0.0002% by mass, a large amount of cost is required. Therefore, the S content is preferably 0.0002% by mass or more. When the content of niobium is more than 0.003 mass%, the formation of nitride becomes remarkable, and magnetic properties are deteriorated. Further, when the content of cerium is more than 0.003 mass%, there is a case where a surface defect called blistering is generated during the casting of steel. 201139699 Therefore, the N content is made 0.003 mass% or less. On the other hand, in the industry, in order to reduce the N content to less than 〇._4% by mass, a large amount of cost is required. Therefore, the N content is preferably 〇.〇〇〇4% by mass or more. w reacts with c to form a carbide and suppresses precipitation of Cr-based carbide. It also suppresses magnetic attenuation. When the W content is less than 〇3 mass%, it is difficult to sufficiently obtain such effects. Most of the (tetra) carbides are precipitated to the grain boundaries and the like. On the other hand, when the W content is more than 0.01% by mass, the amount of the trade-off carbide becomes excessive and the magnetic properties are lowered. Therefore, the content of 1 is set to 〇3 mass% to 〇1 mass%. In order to further suppress the precipitation of Cr-based carbides, the w content is preferably 0.0005 Berry% or more. In addition, as long as the w content is 〇〇〇5 mass%, precipitation of Cr-based carbides can be sufficiently suppressed. Therefore, the stomach content is preferably 0.005% by mass or less from the viewpoint of cost. In addition, in the non-oriented electrical steel sheet having a content of 2% by mass or less, when the Cr content is less than 0.3% by mass, the growth of the W-based carbide is inhibited, and the growth of the crystal grains is hindered, and the magnetic properties are lowered. Therefore, when W is contained in the non-oriented electrical steel sheet having a &S amount of 2% by mass or less, it is important that the Cr content is 0.3% by mass or more. According to the non-oriented electrical steel sheet according to the present embodiment, even if Cr is contained, since an appropriate amount of w is contained, brittleness can be avoided, specific resistance can be increased, and precipitation of Cr-based carbide and magnetic attenuation can be suppressed at a low cost, and the height is increased. Frequency characteristics. Therefore, this embodiment is suitable for high frequency applications. In the low-Si-based non-oriented electrical steel sheet containing no Cr, the growth of the precipitated crystal grains is inhibited, but in the present embodiment, Cr is contained in an amount of 3% by mass or more. Therefore, the w-based carbide is extremely difficult to precipitate. Therefore, by actively utilizing W, precipitation of Cr-based carbides can be suppressed, and 201139699 improves magnetic properties. Further, the non-oriented electrical steel sheet of the present embodiment further contains a mass selected from Mo: 0.001. /. ~0.03 mass%, Ti: 0.0005 mass% - 0.007 mass%, and Nb: 0.0002 mass% - 0.004 mass ° /. At least one of the groups formed is preferred.

Similarly to W, Mo reacts with C to form a carbide, and suppresses precipitation of a Cr-based carbide. Mo also inhibits magnetic attenuation. When the Mo content is less than 0.001% by mass, such effects are not easily obtained. On the other hand, when the Mo content is more than 0.03 mass%, the amount of the Mo-based carbide becomes excessive and the magnetic properties are lowered. Therefore, the Mo content is preferably 0.001% by mass to 〇.3% by mass. In order to further suppress the precipitation of the carbide, the Mo content is preferably 〇·〇〇2 mass 0/〇 or more. In addition, as long as the Mo content is 〇〇2% by mass, the precipitation of & carbides can be sufficiently suppressed. Therefore, the Mo content is preferably 0.02% by mass or less from the viewpoint of cost.

Ti also reacts with c to form carbides in the same manner as w, and suppresses precipitation of Cr-based carbides. Ti also suppresses magnetic attenuation. When the content of butyl sulfonium is less than 〇 5 mass / 〇, it is difficult to sufficiently obtain such effects. On the other hand, when the content of butyl i is more than 0.007 mass%, the amount of butyl stellate carbide becomes excessive and the magnetic properties are lowered. Therefore, the niobium content is preferably 0.0005 mass% to 0.007 mass%. In order to further suppress the precipitation of Cr-based carbides, the niobium content is preferably 7% by mass or more. Further, in order to suppress excessive precipitation of Ti-based carbides, the Ti content is preferably 5% by mass or less.

Similarly to W, Nb reacts with c to form a carbide, and suppresses the precipitation of & Nb also inhibits magnetic attenuation. When the sNb content is less than 〇 2 mascara%, it is difficult to sufficiently obtain such effects. On the other hand, when the amount of Nb contains 10 201139699 is more than 0 - 004% by mass, the amount of Nb-based carbides becomes excessive, and the growth of crystal grains which are recrystallized and annealed is hindered. Therefore, the Nb content is preferably 0.0002% by mass to 0.004% by mass. In order to further suppress the precipitation of the lanthanoid carbide, the Nb content is preferably 0.0003 mass% or more. Further, in order to suppress excessive precipitation of the Nb-based carbide, the Nb content is preferably 0.0035 mass% or less. Further, as described above, Mo, Ti, and Nb exhibit the same effects as W, but W is more effective than Mo, Ti, and Nb. Further, when M〇, Ti and/or Nb in the above range are contained, the retardation of the growth of the crystal grains by the recrystallization annealing of the w-based carbide is less likely to occur than in the case where none of the above is included. Therefore, it is preferable to include at least one selected from the group consisting of Mo, Ti, and Nb to contain all of the three elements. This is because when Mo, Ti and/or Nb are contained in addition to w, the precipitation of Cr-based carbides and the precipitation of snow-based carbon (magnetic attenuation) are particularly effectively suppressed. Further, the non-oriented electrical steel sheet according to the present embodiment may further contain V: 0.0005 mass% to 0.005 mass%, Zr: 0.0002 mass% to 0.003 mass%, and Cu: 0.001 mass% to 〇: )_ Quality. /〇,Sn: 〇 〇〇1 Quality. ~0.2 quality. /. Ni: 0.001% by mass to 0.2% by mass. /〇, %: 0.001 mass% to 0.2 mass%, REM (rare earth element): 0.0002 mass% to 〇4 mass%, and Ca: 0.0005 mass% to 0.006 mass%. Similarly to W, V reacts with C to form a carbide, and suppresses the precipitation of carbonaceous material. The V content is less than 0_0005 mass. When /〇, it is not easy to get this effect adequately. On the other hand' even if the V content is more than 0.005 mass. /〇, still can not get the effect of the content, so that the cost rises significantly. Further, the amount of the V-based carbide 201139699 is excessive, and the growth of the crystal grains subjected to recrystallization annealing is hindered. Therefore, the V content is preferably 5% by mass to 5% by mass.

Similarly to w, Zr reacts with c to form a carbide, thereby suppressing the precipitation of Cr-based carbide. The content of the Ζι· content is less than the G._2f amount, and it is not easy to sufficiently obtain this effect. On the other hand, even if the Zr content is more than 〇〇〇3 mass%, the effect of the content is obtained, and the cost is remarkably increased. Further, the amount of Zr-based carbides is excessive, and the growth of crystal grains subjected to recrystallization annealing is inhibited. Therefore, the content of Zr is preferably 0002.00% by mass to 〇〇〇3% by mass.

Cu, Sn, Ni, and Sb improve aggregate organization. When the content is less than 0.001% by mass, respectively, the effect is not sufficiently obtained, and when the content is more than 0.2% by mass, the cost increases. Therefore, the contents of Cu, Sn, Ni and Sb are preferably 0.001% by mass to 〇.2% by mass, respectively. REM and Ca form coarse oxysulfides to make s harmless. When the REM content is less than 0.0002% by mass and the 〇3 content is less than 5% by mass, the effect is not sufficiently obtained. On the other hand, when the REM content is more than 〇4% by mass and the Ca content is more than 0.006% by mass, the cost increases. Therefore, the REM content is 0.0002% by mass to 0.004% by mass. Preferably, the Ca content is preferably 0.0005 mass% to 0.006 mass%. Thus, when V and/or Zr are also contained, precipitation of Cr^ and carbide can be further suppressed, and for example, magnetic attenuation at a low temperature of 75 (TC or lower) can be further suppressed. Further, such W, Mo, Ti, Nb V, Zr, etc. can be contained in a non-oriented electrical steel sheet by being added to molten steel. Therefore, it is also industrially possible to produce such a non-oriented electrical steel sheet. Next, a method of manufacturing a non-oriented electrical steel sheet will be described. 12 201139699 First, in the usual way, by adjusting the molten steel of the composition, the composition of the molten steel is made from the (new), the flat embryo is added, and the n-rolling is carried out. The temperature of the flat embryo heating is not In particular, it is limited to the formation of fine precipitates, for example, 95 〇. (:: For the sake of suppression, the thickness of the hot-rolled sheet obtained by hot rolling (4) is not specially made, = about 0.8 mm to 3.0 mm. The receiver 'anneals the hot-rolled sheet as needed (hot-rolled sheet annealing). By performing hot-rolled sheet annealing to increase the magnetic flux density, the hysteresis loss can be reduced. The temperature of the annealing of the secret plate is not particularly limited, for example, , (a) just. c is around. After 'following The thickness of the cold-rolled sheet obtained by cold rolling is not particularly limited, but is preferably a high-frequency magnetic property, for example, a thickness as thin as about 0.1 mm to 0.35 mm. When the thickness is more than 0.35 mm, the eddy current loss becomes large, and the high-frequency iron loss is liable to be deteriorated. Further, when the thickness of the cold-rolled sheet is less than 〇.lmm, the productivity is liable to decrease. After the cold emulsion is delayed, the cold-rolled sheet is used. Degreasing and recrystallization annealing to grow crystal grains. In the recrystallization annealing, for example, continuous annealing is performed. The annealing temperature is not particularly limited, and is, for example, 80 Å. (: ~1100. (: Left and right. The particle size of the crystal grains after annealing is preferably 3 〇 μηι 丨 2 〇 μ η η 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 Then, an insulating film of an insulating film is formed by coating and baking a predetermined coating liquid, and for example, an organic insulating film, an inorganic insulating film, or a mixed insulating film containing an inorganic substance and an organic substance is formed. Directionality 13 201139699 The non-oriented electrical steel sheet produced by the company is processed at the customer's end after shipment. For example, it is stamped into a core shape, laminated, and shrink-fit, and is about 700 ° C to 800 ° C. The stress relief annealing, etc. The iron core of the motor can be formed by the series of processes. In addition, the non-oriented electrical steel sheet which is not subjected to stress relief annealing after lamination is called a fu tj process material. The non-oriented electrical steel sheet subjected to the stress relief annealing is referred to as a semi process material. [Examples] Next, an experiment conducted by the inventors of the present invention will be described. The conditions of the experiments and the like are used to confirm the implementation possibilities and effects of the present invention. The invention is not limited by the examples. First, a molten steel containing a surface and a component shown in Table 2, and the remainder consisting of Fe and unavoidable impurities was produced using a laboratory vacuum furnace, and the molten steel was cast to obtain a crude steel. The numerical values in the form of bold lines indicate that the value is outside the scope of the invention. Next, hot rolling of the crude steel was carried out to obtain a hot rolled sheet having a thickness of 2 mm. Thereafter, the N2 gas ambient gas towel was reduced by IGGGt; U minutes. Then, pickling and cold rolling were carried out to obtain a cold-rolled sheet having a thickness of 0.30 mm. Then, recrystallization annealing is carried out in a mixed gas atmosphere of 5% by volume of gas and 50% of N2 gas. The recrystallization annealing roll was subjected to a soaking treatment for 3 G seconds. Thereafter, the steel sheet after recrystallization annealing was punched into a sample having a side length of just _. 14 201139699 [Table 1] Sample No. Component (% by mass) Preparation C Cr Si A1 Μη SNW Mo Ti Nb V Zr 1 0.0005 2.1 2.3 1.2 0.6 0.001 0.0014 0.004 0.01 0.004 0.002 0.001 0.0006 Inventive Example 2 0.0058 2.1 2.3 1.2 0.6 0.001 0.0014 0.004 0.01 0.004 0.002 0.001 0.0006 Inventive Example 3 0.0062 2.1 2.3 1.2 0.6 0.001 0.0014 0.004 0.01 0.004 0.002 0.001 0.0006 Comparative Example 4 0.0095 2.1 2.3 1.2 0.6 0.001 0.0014 0.004 0.01 0.004 0.002 0.001 0.0006 Comparative Example 5 0.0035 0.2 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Comparative Example 6 0.0035 0.4 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Inventive Example 7 0.0035 1.6 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Inventive Example 8 0.0035 5.0 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Inventive Example 9 0.0035 5.4 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Comparative Example 10 0.0035 8.5 1.9 1.4 0.1 0.003 0.0005 0.005 0.001 0.002 0.0002 0.005 0.0003 Comparative Example 11 0.0057 2.5 3.2 0.7 0.2 0 .0002 0.0014 0.0001 0.0003 0.0001 0 0.0001 0 Comparative Example 12 0.0057 2.5 3.2 0.7 0.2 0.0002 0.0014 0.0003 0.0003 0.0001 0 0.0001 0 Inventive Example 13 0.0057 2.5 3.2 0.7 0.2 0.0002 0.0014 0.0005 0.0003 0.0001 0 0.0001 0 Inventive Example 14 0.0057 2.5 3.2 0.7 0.2 0.0002 0.0014 0.006 0.0003 0.0001 0 0.0001 0 Inventive Example 15 0.0057 2.5 3.2 0.7 0.2 0.0002 0.0014 0.010 0.0003 0.0001 0 0.0001 0 Inventive Example 16 0.0057 2.5 3.2 0.7 0.2 0.0002 0.0014 0.013 0.0003 0.0001 0 0.0001 0 Comparative Example 17 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.0008 0.0001 0.004 0.0001 0.0001 Inventive Example 18 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.0012 0.0001 0.004 0.0001 0.0001 Inventive Example 19 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.003 0.0001 0.004 0.0001 0.0001 Inventive Example 20 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.020 0.0001 0.004 0.0001 0.0001 Inventive Example 21 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.030 0.0001 0.004 0.0001 0.0001 Inventive Example 22 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.033 0.0001 0.004 0.0001 0.0001 Comparative Example 23 0.0042 5.0 1.5 0.4 0.5 0.002 0.0027 0.003 0.05 0.0001 0.004 0.0001 0.0001 Comparative Example 24 0.0038 1.1 3.3 2.5 1.4 0.002 0.0011 0.01 0.02 0.0003 0.0001 0.003 0.002 Inventive Example 25 0.0038 1.1 3.3 2.5 1.4 0.002 0.0011 0.01 0.02 0.0007 0.0001 0.003 0.002 Inventive Example 26 0.0038 1.1 3.3 2.5 1.4 0.002 0.0011 0.01 0.02 0.0032 0.0001 0.003 0.002 Inventive Example 27 0.0038 1.1 3.3 2.5 1.4 0.002 0.0011 0.01 0.02 0.0069 0.0001 0.003 0.002 Inventive Example 28 0.0038 1.1 3.3 2.5 1.4 0.002 0.0011 0.01 0.02 0.0074 0.0001 0.003 0.002 Comparative Example 29 0.0015 1.6 2.8 0.6 0.1 0.001 0.003 0.0007 0.005 0.003 0.0001 0 0.001 Inventive Example 30 0.0015 1.6 2.8 0.6 0.1 0.001 0.003 0.0007 0.005 0.003 0.0002 0 0.001 Inventive Example 31 0.0015 1.6 2.8 0.6 0.1 0.001 0.003 0.0007 0.005 0.003 0.0020 0 0.001 Inventive Example 32 0.0015 1.6 2.8 0.6 0.1 0.001 0.003 0.0007 0.005 0.003 0.0040 0 0.001 Inventive Example 33 0.0015 1.6 2.8 0.6 0.1 0.001 0.003 0.0007 0.005 0.003 0.0045 0 0.001 Comparative Example 34 0.0051 0. 5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0003 0.001 Inventive Example 35 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0005 0.001 Inventive Example 36 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0021 0.001 Inventive Example 37 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0049 0.001 Inventive Example 38 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0056 0.001 Comparative Example 39 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0001 0.0001 Inventive Example 40 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0001 0.0003 Inventive Example 41 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0001 0.0015 Inventive Example 42 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0001 0.0028 Inventive Example 43 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.002 0.0028 Inventive Example 44 0.0051 0.5 4.0 1.7 0.3 0.001 0.0004 0.001 0.01 0.002 0.0007 0.0001 0.0035 Comparative Example 15 201139699 % The present invention EXAMPLES OF THE INVENTION Example of the invention Example of the invention Example of the invention ¢3 〇0.0002 ο ο 0.0001 0.003 REM 〇ο ο ο 0.0005 〇〇0.0002 0.0002 g ο ο 0.0001 0.0002 0.0002 CN 0.0001 0.0001 〇0.0001 κη Ο Ο Ο 0.0001 0.0002 〇5 0.0005 Ο 0.0001 0.0001 〇N 0.0028 0.0028 0.0028 0.0028 0.0028 0.0028 > 0.002 0.002 0.002 0.002 0.002 0.002 Ingredients (% by mass) 0.0007 0.0007 0.0007 0.0007 0.0007 0.0007 0.002 0.002 0.002 0.002 0.002 0.002 〇〇〇ο ο ο ο 1—Η ο ο ο ο ο 0.001 0.001 0.001 0.001 0.001 0.001 Z 0.0004 0.0004 0.0004 0.0004 0.0004 0.0004 C/3 0.001 0.001 0.001 0.001 0.001 0.001 CS Ο ο ο ro d rn <t^; Λ Λ p — ρ ο — ρ — ρ Inch _ ρ — ύ Ο ο ιη υ 0.0051 0.0051 0.0051 0.0051 0.0051 0.0051 ζ· 201139699 In addition, the iron loss and magnetic flux density of each sample were measured. The iron loss was measured at an iron loss (W10/400) at a frequency of 400 Hz and a maximum magnetic flux density of 1.0T. Further, the average value of the value at the time of magnetization in the rolling direction and the value in the direction perpendicular to the direction (plate width direction) was calculated. Further, the magnetic flux density was measured at a magnetic flux density (B50) at a frequency of 50 Hz and a maximum magnetization of 5000 A/m. These results are shown in Table 3, “Before Heat Treatment”. After the iron loss and the magnetic flux density were measured, annealing was performed at 450 ° C for 2 hours in an N 2 gas atmosphere. Further, the iron loss and the magnetic flux density of each sample were measured again. The results are shown in the "After Heat Treatment" column of Table 3. 17 201139699 [Table 3] Sample No Heat treatment after lean heat treatment Preparation W10/400 (W/kg) B50(T) W10/400(W/kg) B50(T) 1 13.4 1.665 13.4 1.665 Inventive Example 2 13.4 1.664 13.4 1.664 Inventive Example 3 13.5 1.662 14.3 1.661 Comparative Example 4 13.7 1.660 15.9 1.657 Comparative Example 5 15.9 1.687 15.9 1.687 Comparative Example 6 14.6 1.687 14.6 1.687 Inventive Example 7 13.9 1.635 13.9 1.635 Inventive Example 8 12.6 1.570 12.7 1.567 Inventive Example 9 12.6 1.569 13.6 1.565 Comparative Example 10 11.9 1.541 14.9 1.536 Comparative Example 11 13.1 1.627 15.7 1.627 Comparative Example 12 13.1 1.627 13.4 1.627 Inventive Example 13 13.1 1.627 13.3 1.627 Inventive Example 14 13.1 1.627 13.2 1.627 Inventive Example 15 13.2 1.627 13.2 1.627 The present invention Example 16 14.1 1.627 14.1 1.627 Comparative Example 17 13.5 1.602 13.7 1.598 Inventive Example 18 13.5 1.602 13.7 1.602 Inventive Example 19 13.5 1.602 13.7 1.602 Inventive Example 20 13.5 1.602 13.7 1.602 Inventive Example 21 13.5 1.602 13.6 1.602 Inventive Example 22 14.3 1.603 14.3 1.600 Comparative Example 23 16.7 1.604 16.7 1.599 Comparative Example 24 12.6 1.611 12.8 1.608 EXAMPLE 25 12.6 1.611 12.8 1.611 Inventive Example 26 12.6 1.611 12.8 1.611 Inventive Example 27 12.7 1.611 12.8 1.611 Inventive Example 28 13.1 1.612 13.6 1.612 Comparative Example 29 13.4 1.639 13.5 1.636 Inventive Example 30 13.4 1.639 13.5 1.639 Inventive Example 31 13.4 1.639 13.5 1.639 Inventive Example 32 13.5 1.639 13.5 1.639 Inventive Example 33 14.8 1.640 14.8 1.640 Comparative Example 34 10.9 1.621 11.0 1.619 Inventive Example 35 10.9 1.621 10.9 1.621 Inventive Example 36 10.9 1.621 10.9 1.621 Inventive Example 37 10.9 1.621 10.9 1,621 Inventive Example 38 11.5 1.621 11.5 1.621 Comparative Example 39 10.9 1.595 11.0 1.595 Inventive Example 40 10.9 1.595 10.9 1.595 Inventive Example 41 10.9 1.595 10.9 1.595 Inventive Example 42 10.9 1.595 10.9 1.595 Inventive Example 43 10.9 1.595 10.9 1.595 The present invention Example 44 11.3 1.595 11.3 1.595 Comparative Example 45 10.9 1.602 10.9 1.602 Inventive Example 46 10.9 1.605 10.9 1.605 Inventive Example 47 10.9 1.604 10.9 1.604 Inventive Example 48 10.9 1.607 10.9 1.607 Inventive Example 49 10.9 1.611 10.9 1.611 Inventive Example 50 10.9 1.601 10.9 1.601 this Inventive Example 18 201139699 As shown in Table 3, the samples No. 1 to No. 2, Ν〇.6 to Ν〇.8, Ν〇·12~Ν〇.15, Ν〇.17~Ν to which the scope of the present invention belongs are shown. 〇·21, Ν〇.24~Ν〇.27,

No.29~No.32 'No.34~No.37 'No.39~No.43 ' ^Νο.45~Νο.5〇 Low iron loss can be obtained before and after heat treatment. In other words, before the heat treatment, a low iron loss can be obtained because a sufficient size of crystal grains can be obtained, and after the heat treatment, low iron loss can be maintained by suppressing the precipitation of Cr糸 carbide. Further, as a result of comparison between the sample No. 43 and the sample Νο·45~Νο·50, it is understood that the magnetic flux density is increased when at least one selected from the group consisting of Cu, Sn, Ni, Sb, REM, and Ca is contained. On the other hand, in the samples No. 3 to No. 4, since the C content was too high, a large amount of carbide precipitated with heat treatment showed a significant deterioration in iron loss. In the sample N〇.5, the iron loss is large because the Cr content is too low. In sample No. 9 to No. 10, since the Cr content was too south, a large amount of Cr-based carbide was precipitated, and the deterioration of iron loss was remarkable. In the sample No. 11, when the W content was too low, a large amount of Cr-based carbide was precipitated, and the deterioration of the iron loss was remarkable. In sample No. 16, since the W content was too high, the iron loss was large. In samples No. 22 to No. 23, since the Mo content was too high, the iron loss was large. In sample No. 28, since the Ti content was too high, the iron loss was large. In sample No. 33, the iron loss was large because the Nb content was too high. In the sample N〇38, since the V content is too high, the V-based carbide precipitates excessively, and the growth of the crystal grains which are recrystallized and annealed is hindered as a sample which is the same as the component other than V. 1^〇.34~]^〇. 37, the iron loss becomes high. In the sample]^〇_44, because the 21' content is too high,

Zr-based carbides are excessively precipitated, and the growth of crystal grains which are recrystallized and annealed is hindered. The sample having the same composition as that of Zr is Νο·39~N〇, and the iron loss is high. Further, although the iron loss of the samples No. 38 and No. 44 was lower than that of the invention example of the present invention, the cost was not significantly improved, and the cost was significantly increased. Further, as shown in Table 3, in Sample No. 11 in which the W content differs only between samples No. 11 to No. 16 in which the W content is different, and the W content is less than the lower limit of the range of the present invention, the iron loss deterioration accompanying the heat treatment is remarkable. . From this, it is understood that W can suppress deterioration of iron loss accompanying heat treatment. Further, in samples No. 30 to No. 32 having a low W content, since an appropriate amount of Mo, Ti, and Nb were also contained, deterioration of iron loss accompanying heat treatment was almost suppressed. From this, it is understood that the effect is particularly large when a predetermined amount of Mo, Ti, and Nb are contained. In addition, the samples Νο·34~No.37, and Νο.39~Νο·43* have extremely low iron loss because they contain an appropriate amount of V and Zr. Industrial Applicability The present invention can be applied to, for example, the electromagnetic steel sheet manufacturing industry and the electromagnetic steel sheet utilization industry. t diagram simple description 3 (none) [main component symbol description] (none) 20

Claims (1)

201139699 VII. Patent application scope: 1. A non-oriented electrical steel sheet characterized by comprising: Cr: 0.3% by mass to 5.3% by mass; Si: 1.5% by mass to 4% by mass; 'A1: 0.4% by mass to 3 % by mass; and W: 0.0003% by mass to 0.01 mass 0/〇, C content is 0.006 mass% or less, Μη content is 1.5 mass% or less, S content is 0.003 mass% or less, and cerium content is 0.003 mass% or less, and the remainder Part of it consists of Fe and unavoidable impurities. 2. The non-oriented t-magnetic steel sheet according to item 1 of the patent application is further selected from the group consisting of Mo: 0.001% by mass to 0.03 mass%/〇, Ti: 0.0005 mass% to 0.007 mass%, and Nb: 0.0002 It is composed of at least one of mass% to 0.004% by mass. 3. The non-oriented electrical steel sheet according to claim 1, further comprising V: 0.0001 mass% to 0.005 mass%, Zr: 0.0003 mass% to 0.003 mass%, and Cu: 0.001 mass. ～0.2% by mass, Sn: 0.001% by mass to 0.2% by mass, Ni: 0.001% by mass to 0.2% by mass, Sb: 0.001% by mass to 0.2% by mass, rare earth elements: 0.0002% by mass to 0.004% by mass, and Ca: 0.0005 At least one of the groups consisting of % by mass to 0.006 mass%. 4. The non-oriented electrical steel sheet according to claim 2, further comprising a mass selected from the group consisting of V: 0.0005 mass% to 0.005 mass. /. Zr: 0.0003% by mass to 0.003 mass%, and Cu: 0.001 mass%/. ～0.2% by mass, Sn: 0.001% by mass to 0.2% by mass, Ni: 0.001% by mass to 0.2% by mass, 21 201139699 Sb: 0.001% by mass to 0.2% by mass, rare earth element: 0.0002% by mass to 0.004% by mass, and Ca : at least one of the group consisting of 0.0005 mass% to 0.006 mass%. 22 201139699 IV. Designated representative map: (1) The representative representative of the case is: ( ). (None) (2) A brief description of the symbol of the representative figure: (none) 5. If there is a chemical formula in this case, please disclose the chemical formula that best shows the characteristics of the invention: